Non-aqueous electrolyte secondary battery

ABSTRACT

A non-aqueous electrolyte secondary battery including: a positive electrode; a negative electrode; a separator interposed between the positive electrode and the negative electrode; a non-aqueous electrolyte; and a porous insulating film adhered to a surface of at least one selected from the group consisting of the positive electrode and the negative electrode, the porous insulating film including an inorganic oxide filler and a film binder, wherein the ratio R of actual volume to apparent volume of the separator is not less than 0.4 and not greater than 0.7, and wherein the ratio R and a porosity P of the porous insulating film satisfy the relational formula: −0.10≦R−P≦0.30.

RELATED APPLICATIONS

This application is a Divisional of U.S. application Ser. No.10/562,438, filed Dec. 28, 2005, now U.S. Pat. No. 7,422,825 which is aU.S. National Phase under 35 U.S.C. §371 of International ApplicationNo. PCT/JP2005/005158, filed Mar. 22, 2005, claiming priority ofJapanese Application Nos. 2004-098985, filed Mar. 30, 2004; 2004-173734,filed Jun. 11, 2004; and 2004-183948, filed Jun. 22, 2004, the entirecontents of each of which are hereby incorporated by reference.

TECHNICAL FIELD

The present invention relates to a non-aqueous electrolyte secondarybattery, and more particularly to a lithium ion secondary batterycomprising a porous insulating film adhered to an electrode surface andhaving excellent thermal resistance, safety against short-circuit anddischarge characteristic.

BACKGROUND ART

Since lithium ion secondary batteries have a high electromotive forceand high energy density, they are employed as main power sources formobile communication devices and portable electronic devices. A typicallithium ion secondary battery comprises a positive electrode composed ofa lithium composite oxide, a negative electrode composed of a materialcapable of absorbing and desorbing lithium ions, a separator interposedbetween the positive electrode and the negative electrode, and anon-aqueous electrolyte.

Separators serve to electronically insulate the positive electrode andthe negative electrode from each other as well as to retain anon-aqueous electrolyte. A separator is typically produced by molding apolyolefin resin or the like into a sheet form. Separators usuallydeform at a temperature of 120° C. to 160° C. For this reason, when asharp projection such as a nail penetrates a separator (e.g., as in thenail penetration test), the separator deforms around the projection dueto heat that is instantly generated by short-circuiting, therebyenlarging the short-circuited area. As a result, the battery might reachan overheated state.

In order to cope with the problem, it has been proposed to adhere a filmcontaining an inorganic oxide such as alumina and a binder on thesurface of either positive electrode or negative electrode (see JapaneseLaid-Open Patent Publication No. Hei 7-220759). However, when a film isadhered to the electrode surface, discharge characteristic of thebattery, namely, discharge characteristic in a low temperatureenvironment or during large current discharge might be deterioratedsignificantly.

Also, a technique is proposed to enhance the shut-down effect of a filmin the event of internal short-circuit by forming the film composed of aresin material having a high bulk density on an electrode (see JapaneseLaid-Open Patent Publication No. Hei 11-144706). The effect ofinhibiting ion migration obtained by allowing the resin forming aseparator or film to soften and closing the pore structure is calledshut-down effect.

In order to allow such a film to exhibit its shut-down effect in theevent of internal short-circuit, it is necessary to set the glasstransition temperature of the resin material at a low level. During thenail penetration test, however, the short-circuited area could locallyhave a temperature of over several hundred degrees although thetemperature may vary depending on the test conditions. Accordingly,there is a possibility that the resin having a low glass transitiontemperature might be excessively softened or burned out, and theshort-circuited area might be enlarged.

Proposals are also made from the viewpoint of preventing an internalshort-circuit due to the asperity of electrode surface, one of which isa technique to form a film composed of an inorganic oxide filler such asalumina and a water soluble polymer on an electrode (see JapaneseLaid-Open Patent Publication No. Hei 9-147916). The use of a filmcomposed of an inorganic oxide filler having superior thermal resistanceand a water soluble polymer prevents the film from deforming in theevent of internal short-circuit.

However, polymers often swell by absorbing a liquid component fordispersing the raw material of the film during the formation of the filmor absorbing an electrolyte during charge/discharge. If the film swells,the number of ion migration paths is decreased, resulting in low ionconductivity between the electrode plates, which makes it difficult tomaintain discharge characteristic of the battery. Therefore, unlesssomething is done to prevent the swelling of the film, even if improvedsafety against short-circuit is achieved, it is difficult to keepdischarge characteristic of the battery.

Meanwhile, from the viewpoint of preventing dendrites, a technique isproposed in which a separator composed of a polymer layer having aporous structure and a ceramic composite layer containing inorganicparticles is used (see Japanese Laid-Open Patent Publication No.2001-319634). Further, in the event of lacking an electrolyte betweenthe positive and negative electrodes due to the swelling of theelectrodes, from the viewpoint of supplying an electrolyte to betweenthe electrodes, a technique is proposed in which anelectrolyte-retaining layer including inorganic particles dispersedtherein is formed on the side of a separator in contact with a negativeelectrode (Japanese Laid-Open Patent Publication No. 2002-8730).

The foregoing improvement techniques (e.g., Japanese Laid-Open PatentPublications Nos. 2001-319634 and 2002-8730) are intended to preventdendrites or to improve high rate discharge characteristic, and they donot deal with safety against internal short-circuit and safety at thetime of nail penetration test. The ceramic composite layer is a part ofthe separator and the electrolyte-retaining layer is integrated with theseparator. Accordingly, in the event of internal short-circuit, theceramic composite layer and the electrolyte-retaining layer will alsodeform due to heat generated from the short circuit reaction.

DISCLOSURE OF INVENTION

An object of the present invention is to provide a non-aqueouselectrolyte secondary battery comprising a porous insulating filmadhered to an electrode surface which can prevent the deterioration ofdischarge characteristic particularly during low temperature dischargeor during large current discharge and can provide excellent safety.

Another object of the present invention is to provide a non-aqueouselectrolyte secondary battery comprising a porous insulating filmadhered to an electrode surface which can provide excellent thermalresistance, great safety against short-circuit and superior dischargecharacteristic by relieving the effect resulting from the swelling ofthe porous insulating film.

Yet another object of the present invention is to provide a non-aqueouselectrolyte secondary battery comprising a porous insulating filmadhered to an electrode surface which can provide excellent thermalresistance, great safety against short-circuit and superior dischargecharacteristic by improving the adhering interface between the porousinsulating film and the electrode surface.

Having conducted extensive studies, the present inventors have revealedthat, although discharge characteristic can be improved by increasingthe porosities of a porous insulating film and a separator, excessivelyincreased porosities of a porous insulating film and a separator causesome drawbacks. More specifically, it was revealed that the shut-downcharacteristics of the porous insulating film and the separatordecreases, and electric current continuously flows with low resistanceeven after shut-down, which increases the battery temperature. As aresult, the present inventors have discovered that both a high level ofsafety and satisfactory discharge characteristic can be achieved byoptimally designing the porosities of a porous insulating film and aseparator.

Based on the above findings, the present invention has beenaccomplished. A first embodiment of the present invention relates to anon-aqueous electrolyte secondary battery comprising: a positiveelectrode; a negative electrode; a separator interposed between thepositive electrode and the negative electrode; a non-aqueouselectrolyte; and a porous insulating film adhered to a surface of atleast one selected from the group consisting of the positive electrodeand the negative electrode, wherein the ratio R of actual volume toapparent volume of the separator is not less than 0.4 and not greaterthan 0.7, and wherein the ratio R and a porosity P of the porousinsulating film satisfy the relational formula:−0.10≦R−P≦0.30.

The porous insulating film comprises an inorganic oxide filler and afilm binder.

Preferably, 90% cumulative volume pore size D90 in a pore sizedistribution of the porous insulating film measured by a mercuryintrusion porosimetér is not less than 0.15 μm.

Preferably, a void capable of retaining the non-aqueous electrolyte isformed on an adhering interface where the porous insulating film adheresto the electrode surface. In this case, a void size distribution of theadhering interface measured by a mercury intrusion porosimeterpreferably has a peak in a region ranging from 1 to 4 μm. The electrodesurface to which the porous insulating film adheres preferably has anaverage surface roughness Ra of 0.1 to 1 μm. Further, the rate of thevoid volume on the adhering interface to the total volume of pores ofthe porous insulating film is preferably 15 to 25%.

The inorganic oxide filler preferably comprises polycrystallineparticles. Preferably, the polycrystalline particles each comprise aplurality of primary particles that are diffusion-bonded together. Theprimary particles forming the polycrystalline particles preferably havean average particle size of not greater than 3 μm, more preferably notgreater than 1 μm. The average particle size of the polycrystallineparticles is not less than twice the average particle size of theprimary particles forming the polycrystalline particles, and not greaterthan 10 μm, more preferably not greater than 3 μm. More preferably, theprimary particles have an average particle size of not greater than 1μm, and the polycrystalline particles have an average particle size ofnot greater than 3 μm.

The amount of the film binder contained in the porous insulating film ispreferably not greater than 4 parts by weight per 100 parts by weight ofthe inorganic oxide filler. Further, the amount of the film bindercontained in the porous insulating film is preferably not less than 1part by weight per 100 parts by weight of the inorganic oxide filler.

According to the present invention, it is possible to provide anon-aqueous electrolyte secondary battery comprising a porous insulatingfilm adhered to an electrode surface which can prevent the deteriorationof discharge characteristic of the battery and provide excellentshut-down effect. At the same time, safety against short-circuit can beensured. More specifically, the shut-down effect, which increasesresistance whenever necessary so as to shut down electric current, canalso be enhanced while the discharge characteristic of the battery ismaintained at a satisfactory level when the ratio R of actual volume toapparent volume of the separator is not less than 0.4 and not greaterthan 0.7, and the ratio R and a porosity P of the porous insulating filmsatisfy the relational formula:−0.10≦R−P≦0.30.

When 0.4≦R≦0.7 and −0.10≦R−P≦0.30 are satisfied, two effects arebelieved to contribute to the increase of internal resistance: theeffect of inhibiting ion migration which is brought about by closing thepore structure; and the effect of inhibiting ion migration which isbrought about by intrusion of resin into the voids of a surface portionof the porous insulating film so as to fill the voids with the resin.The former effect is exerted in the entire separator. The latter effectis exerted near the interface between the porous insulating film and theseparator. The former effect, however, may not be obtained when theseparator is thin because, in a thin separator, the constituent resinmostly melts and enters the voids of the electrode. The latter effect,on the other hand, can be obtained regardless of the thickness of theseparator.

When 90% cumulative volume pore size D90 in a pore size distribution ofthe porous insulating film measured by a mercury intrusion porosimeteris not less than 0.15 μm, even if the film binder swells with thenon-aqueous electrolyte, sufficient ion conductivity can be maintainedbecause it is not largely affected by the swelling. In order to optimizethe pore size distribution of the porous insulating film, it ispreferred that the inorganic oxide filler comprise polycrystallineparticles and the polycrystalline particles each comprise a plurality ofprimary particles that are diffusion-bonded together.

Moreover, when a void capable of retaining a non-aqueous electrolyte isformed at the adhering interface between the porous insulating film andan electrode surface, the ion conductivity of the electrode carrying theporous insulating film thereon can be maintained at a satisfactorylevel. Accordingly, the discharge characteristic is also maintained at asatisfactory level.

BRIEF DESCRIPTION OF DRAWINGS

FIG. 1 is a schematic diagram showing a separator and a porousinsulating film in the normal state.

FIG. 2 is a schematic diagram showing a separator and a porousinsulating film in a state at high temperature.

FIG. 3 is an SEM image of a cross section of a negative electrode towhich a porous insulating film is adhered.

FIG. 4 is an SEM image of a cross section of a negative electrode towhich a porous insulating film is adhered.

FIG. 5 is a graph showing the pore size distributions of negativeelectrodes and porous insulating films determined by a mercury intrusionporosimeter.

BEST MODE FOR CARRYING OUT THE INVENTION

A non-aqueous electrolyte secondary battery of the present inventionincludes a positive electrode; a negative electrode; a separatorinterposed between the positive electrode and the negative electrode; anon-aqueous electrolyte; and a porous insulating film adhered to asurface of at least one selected from the group consisting of thepositive electrode and the negative electrode. The separator and theporous insulating film have common functions: both serve toelectronically insulate the positive electrode and the negativeelectrode from each other, and to retain the non-aqueous electrolyte,but they differ significantly in structure.

FIG. 1 schematically shows a separator and a porous insulating film inthe normal state. A porous insulating film 2 has a structure in whichinorganic oxide filler particles 3 are bonded by a film binder (notshown in the diagram). Voids 4 are formed among the inorganic oxidefiller particles. Because a non-aqueous electrolyte infiltrates into thevoids 4, the ions in the electrolyte can easily pass through the porousinsulating film 2. The ions having passed through the porous insulatingfilm 2 reach active material particles 1 forming an electrode, and theelectrode reaction proceeds.

A separator 5 is usually produced by drawing a resin sheet obtained by amolding method such as extrusion molding. The pore structure of theseparator 5 is in the form of a matrix. Accordingly, the separator 5 hasa high tensile strength in the plane direction and is liable to deformwhen exposed at a high temperature. The porous insulating film 2, on theother hand, has a lower tensile strength in the plane direction than theseparator, but it is superior to the separator in that, unlike theseparator 5, the porous insulating film does not deform even whenexposed to a high temperature. Thus, the porous insulating film 2 mainlyhas the function to prevent a short circuit from spreading out in theevent of the occurrence of internal short-circuit. Because the inorganicoxide filler has high thermal resistance, even when a short-circuitedarea is formed during, for example, the nail penetration test, it ispossible to prevent the short-circuited area from enlarging by reactionheat.

When the battery temperature is increased by an external factor andreaches the melting point of the separator 5, the pores of the separatorclose and the internal resistance of the battery increases. In such acase, as shown in FIG. 2, some of the melt resin 5 a infiltrates intothe voids 4 in the surface portion of the porous insulating film 2. Asmore voids 4 are filled with the infiltrated resin 5 a, the internalresistance of the battery increases, which inhibits ion migration. It istherefore possible to shut down electric current effectively. The degreeof the infiltration of the resin 5 a is affected by the density of resinin the separator or the porosity of the porous insulating film 2. Inother words, the shut-down effect can be enhanced by optimizing therelation between the ratio R of actual volume to apparent volume of theseparator and a porosity P of the porous insulating film.

In order to improve the shut-down effect, the ratio R of actual volumeto apparent volume of the separator should be not less than 0.4 and notgreater than 0.7. Further, the ratio R and the porosity P of the porousinsulating film must satisfy the relational formula: −0.10≦R−P≦0.30.When the ratio R is less than 0.4, the shut-down characteristic will below. When the ratio R exceeds 0.7, the discharge characteristic will below. Moreover, when the R−P is less than −0.10, although the separatormelts, the voids of the surface portion of the porous insulating filmwill not be sufficiently filled with the resin, and the shut-down effectwill be low. Conversely, when the R−P exceeds 0.30, the dischargecharacteristic of the battery during low temperature discharge or duringlarge current discharge will be low.

A porosity P of the porous insulating film should be determined so as tosatisfy the range: −0.10≦R−P≦0.30. The porosity P of the porousinsulating film can be determined by the following method. A paint(hereinafter referred to as porous film paint) is first prepared, thepaint containing an inorganic oxide filler, a film binder and adispersing medium for dispersing the filler. The porous film paint isapplied onto a metal foil and dried. The dried film attached to themetal foil is cut into a desired area, from which the metal foil isremoved. Thereby, a sample of the porous insulating film is obtained.From the thickness and area of the obtained sample, the apparent volumeV_(a) of the porous insulating film is determined. Subsequently, theweight of the sample is measured. Using the weight of the sample and theactual specific gravity of the inorganic filler and the film binder, theactual volume V_(t) of the porous insulating film is determined. Fromthe apparent volume V_(a) and the actual volume V_(t), the porosity P iscalculated by the following equation: porosity P=(V_(a)−V_(t))/V_(a).

The ratio R of actual volume to apparent volume of the separator can bedetermined by the following method. The apparent volume V_(as) of theseparator is first calculated from the thickness and area of theseparator. Subsequently, the weight of the separator is measured. Usingthe weight and actual specific gravity of the separator, the actualvolume V_(ts) of the separator is determined. From the apparent volumeV_(as) and the actual volume V_(ts), the ratio R is calculated by thefollowing equation: ratio R=V_(ts)/V_(as).

Although the material for the separator is not specifically limited, theseparator is preferably composed mainly of a resin material having amelting point of not greater than 200° C. Namely, a polyolefin ispreferably used. Particularly preferred are polyethylene, polypropylene,ethylene-propylene copolymers and composites of polyethylene andpolypropylene. This is because a separator made of a polyolefin having amelting point of not greater than 200° C. melts easily in the eventwhere the battery is short-circuited by an external factor. Theseparator may be a single-layer film composed of a single polyolefinresin, or a multilayer film composed of two or more polyolefin resins.Although not specifically limited, the thickness of the separator ispreferably 8 to 30 μm from the viewpoint of maintaining the designcapacity of the battery.

The porous insulating film should be adhered to an electrode surface.This is because, if the porous insulating film is adhered onto aseparator having low thermal resistance, when the separator deforms at ahigh temperature, the porous insulating film also deform. Also, it isnot practical to form a sheet composed of the porous insulating filmalone and to dispose the sheet between positive and negative electrodes,either. In the case of forming a sheet composed of the porous insulatingfilm alone, the thickness of the sheet needs to be increased to aconsiderably large thickness from the viewpoint of retaining thestrength. In addition, it requires a large amount of film binder. Theuse of such a porous insulating film makes it difficult to maintainbattery characteristics and design capacity.

The present invention encompasses all cases where the porous insulatingfilm is placed between positive and negative electrodes. In other words,the present invention includes the following cases: the case where theporous insulating film is adhered to only positive electrode surface;the case where the porous insulating film is adhered to only negativeelectrode surface; and the case where the porous insulating films areadhered to both positive electrode surface and negative electrodesurface, respectively. The present invention further includes thefollowing cases: the case where the porous insulating film is adhered toonly one surface of the positive electrode; the case where the porousinsulating film is adhered to both surfaces of the positive electrode,respectively; the case where the porous insulating film is adhered toonly one surface of the negative electrode; and the case where theporous insulating films are adhered to both surfaces of the negativeelectrode, respectively.

From the viewpoint of providing a porous insulating film having highthermal resistance, it is desirable that the inorganic oxide filler havea thermal resistance of not less than 250° C., and that the inorganicoxide filler be electrochemically stable in the potential window ofnon-aqueous electrolyte secondary batteries. Although many inorganicoxide fillers satisfy these conditions, among inorganic oxides,preferred are alumina, silica, zirconia, titania. Particularly preferredare alumina and titania. The inorganic oxide fillers may be used singlyor in any combination of two or more.

From the viewpoint of providing a porous insulating film havingsatisfactory ion conductivity, the inorganic oxide filler preferably hasa bulk density (tap density) of not less than 0.2 g/cm³ and not greaterthan 0.8 g/cm³. When the bulk density is less than 0.2 g/cm³, theinorganic oxide filler will be too bulky, and the structure of theporous insulating film might be brittle. Conversely, when the bulkdensity exceeds 0.8 g/cm³, it might be difficult to form suitable voidsamong the filler particles. The particle size of the inorganic oxidefiller is not specifically limited, but the smaller the particle size,the lower the bulk density tends to be. Although the particle shape ofthe inorganic oxide filler is not specifically limited, it is desirablyan indefinite-shaped particle comprising a plurality (e.g., about 2 to10, preferably 3 to 5) of primary particles bonded together. Sinceprimary particles usually consist of a single crystal, theindefinite-shaped particle is always a polycrystalline particle.

The amount of the film binder contained in the porous insulating film isdesirably not less than 1 part by weight and not greater than 20 partsby weight relative to 100 parts by weight of the inorganic oxide filler,more desirably, not less than 1 part by weight and not greater than 5parts by weight. When the amount of the film binder exceeds 20 parts byweight, many of the pores in the porous insulating film will be filledwith the film binder, and the discharge characteristic might be low.Conversely, when the amount of the film binder is less than 1 part byweight, the adhesion between the porous insulating film and an electrodesurface will be low, and the porous insulating film might be separatedfrom the electrode surface.

From the viewpoint of maintaining thermal stability of the porousinsulating film even when an area in which an internal short-circuit hasoccurred is heated to a high temperature, the film binder preferably hasa melting point or thermal decomposition temperature of not less than250° C. Further, when the film binder is composed of a crystallinepolymer, the crystalline polymer preferably has a melting point of notless than 250° C. It should be understood that because the porousinsulating film is composed mainly of an inorganic oxide having highthermal resistance, the effect of the present invention is not largelyaffected by the thermal resistance of the film binder.

Examples of the film binder include styrene butadiene rubber (SBR),modified forms of SBR containing an acrylic acid unit or acrylate unit,polyethylene, polytetrafluoroethylene (PTFE), polyvinylidene fluoride(PVDF), tetrafluoroethylene-hexafluoropropylene copolymers (FEP),derivatives of polyacrylic acid and derivatives of polyacrylonitrile.They may be used singly or in any combination of two or more. Amongthem, particularly preferred are derivatives of polyacrylic acid andderivatives of polyacrylonitrile. Preferably, these derivatives furthercontain, in addition to an acrylic acid unit or/and an acrylonitrileunit, at least one selected from the group consisting of methyl acrylateunit, ethyl acrylate unit, methyl methacrylate unit and ethylmethacrylate unit.

When rubber particles (e.g., SBR or its derivative) are used as the filmbinder, the film binder preferably further contains a thickener. As thethickener, it is generally best to select a polymer soluble in adispersing medium for the porous film paint. Examples of such thickenerinclude PVDF and carboxymethyl cellulose (CMC). Also, modifiedacrylonitrile rubber soluble in the dispersing medium may be used.

From the viewpoint of preventing the decrease of discharge performancedue to the swelling of the porous insulating film, desirably, 90%cumulative volume pore size D90 in a pore size distribution of theporous insulating film measured by a mercury intrusion porosimeter isnot less than 0.15 μm. The pore size distribution indicates, forexample, the relation between pore size and volume (frequency) of thepores having the pore size. Cumulative volume is, calculated by addingup the volume of pores from pores having a smaller pore size.

When the pore size D90 is not less than 0.15 μm, even if the film binderin the porous insulating film is swelled with the non-aqueouselectrolyte, it is believed that the pores necessary to ensure ionconductivity will remain in the porous insulating film. When the poresize D90 is less than 0.15 μm, the small pores will account for anexcessively large proportion of the total pores in the porous insulatingfilm, and the porous insulating film will be easily affected by theswelling of the film binder. From the viewpoint of further reducing theeffect due to the swelling of the film binder, the pore size D90 ispreferably not less than 0.2 μm. When the pore size D90 is too large,however, the volume ratio of the pores in the porous insulating filmwill be excess, and the structure of the porous insulating film will bebrittle. Accordingly, the pore size D90 is desirably not greater than 2μm.

From the viewpoint of achieving the pore size distribution as describedabove, the amount of the film binder contained in the porous insulatingfilm is desirably not greater than 4 parts by weight per 100 parts byweight of the inorganic oxide filler, more preferably, not greater than3 parts by weight. The amount of the film binder disposed among theinorganic oxide filler particles should be small: otherwise, it isdifficult to form a porous insulating film having a pore size D90 of notless than 0.15 μm. By reducing the amount of the film binder disposedamong the inorganic oxide filler particles to a small level, theswelling of the porous insulating film can be prevented effectively. Onthe other hand, from the viewpoint of preventing the porous insulatingfilm from separating or dropping from an electrode surface, the amountof the film binder is preferably not less than 1 part by weight per 100parts by weight of the inorganic oxide filler.

From the viewpoint of achieving the pore size distribution as describedabove, the inorganic oxide filler preferably contain polycrystallineparticles having a shape such as dendritic, coral-like or grapebunch-like. Because such polycrystalline particles hardly form anexcessively close-packed structure in the porous insulating film, theyare suitable for forming appropriate voids. Examples of thepolycrystalline particles include particles each comprising about 2 to10 primary particles bonded together by melting and particles eachcomprising about 2 to 10 crystals coalesced by contacting with eachother during the growth of the crystal.

The primary particles forming the polycrystalline particles desirablyhave an average particle size of not greater than 3 μm, more preferablynot greater than 1 μm. When the primary particles have an averageparticle size of exceeding 3 μm, the amount of the film binder will beexcess as the surface area of the filler is decreased, and the swellingof the porous insulating film due to the non-aqueous electrolyte mighteasily occur. In the case where the primary particles cannot beidentified clearly in the polycrystalline particles, the particle sizeof the primary particles is defined by the thickest part of a knot ofthe individual polycrystalline particles.

The average particle size of the primary particles can be determined by,for example, measuring the particle size of at least 10 primaryparticles using an SEM image or TEM image of the polycrystallineparticles, and then calculating the average thereof. When the primaryparticles are heated to be diffusion-bonded to produce polycrystallineparticles, the average particle size (volume based median size: D50) ofthe primary particles serving as the raw material can be treated as theaverage particle size of the primary particles forming thepolycrystalline particles. In the heat treatment only to facilitate thediffusion and bonding, the average particle size of the primaryparticles hardly changes.

The average particle size of the polycrystalline particles is desirablynot less than twice the average particle size of the primary particles,and not greater than 10 μm, more desirably not greater than 3 μm. Theaverage particle size (volume based median size: D50) of thepolycrystalline particles can be measured by, for example, a wet typelaser particle size distribution analyzer available from Microtrac Inc.When the polycrystalline particles have an average particle size lessthan twice that of the primary particles, the porous insulating filmmight have an excessively close-packed structure. When thepolycrystalline particles have an average particle size of exceeding 10μm, the porosity of the porous insulating film might be excess, and thestructure of the porous insulating film might be brittle.

The method for obtaining the polycrystalline particles is notspecifically limited. For example, they can be obtained by baking aninorganic oxide to form a mass and pulverizing the mass into anappropriate size. Alternatively, without performing the pulverizationstep, polycrystalline particles can be directly obtained by allowinggrowing crystals to contact with each other.

For example, when the polycrystalline particles are obtained by bakingα-alumina to form a mass, which is then pulverized into an appropriatesize, the baking temperature is preferably 800 to 1300° C. The bakingtime is preferably 3 to 30 minutes. The pulverization of the mass can bedone by a wet type grinding unit such as ball mill or a dry typegrinding unit such as jet mill or jaw crusher. In this case, thoseskilled in the art can obtain polycrystalline particles having a desiredaverage particle size by appropriately adjusting the pulverizationconditions.

The porous insulating film adhered to an electrode surface is obtainedby first preparing a paint (hereinafter referred to as porous filmpaint) containing an inorganic oxide filler and a film binder, which isthen applied onto an electrode surface, followed by drying. The porousfilm paint is obtained by mixing an inorganic oxide filler and a filmbinder with a dispersing medium for the filler. Preferred examples ofthe dispersing medium include, but not limited to, organic solvents suchas N-methyl-2-pyrrolidone (NMP) and cyclohexanone, and water. Themixture of the filler, the film binder and the dispersing medium can beperformed by using a double arm kneader such as planetary mixer or a wettype disperser such as beads mill. The application of the porous filmpaint on an electrode surface can be done by comma roll method, gravureroll method or die coating method.

It is generally accepted that, when the degree of dispersion of theporous film paint is increased, the film binder covers the inorganicoxide filler more completely, thereby improving the binding capability.On the other hand, when the degree of dispersion of the porous filmpaint is increased, the pore size of the porous insulating film tends tobe small. Conversely, when the degree of dispersion of the porous filmpaint is decreased, the binding capability tends to be low. Further,when the degree of dispersion of the porous film paint is decreased,because the film binder aggregates, the pore size of the porousinsulating film tends to be large. Accordingly, in order to allow theporous insulating film to exhibit sufficient binding capability whilethe pore size D90 is not less than 0.15 mm, it is desirable toappropriately select the dispersion conditions of the porous film paint.

Those skilled in the art can appropriately select the dispersionconditions of the porous film paint according to the intended finalcondition of the paint. Because the state of dispersion of the porousfilm paint varies according to, for example, the mechanism, performancecapability and operation conditions of the equipment used for thepreparation of the porous film paint, the state of dispersion can bereadily controlled by appropriately selecting them. For example, thestate of dispersion of the porous film paint varies between when theequipment is a double arm kneader and when the equipment is a beadsmill. Further, the state of dispersion of the porous film paint variesalso according to the performance capability of the equipment such asthe size or rotation speed of dispersing machine, the amount of rawmaterial for the paint introduced into the dispersing machine, the solidcontent of the paint, or the operation conditions such as stirring time.

From the viewpoint of controlling the degree to which the film bindercovers the inorganic oxide filler, it is desirable to appropriatelyadjust the conditions for applying the porous film paint or theconditions for drying the film. Specifically, it is desirable tofacilitate the aggregation of the film binder to an appropriate level byincreasing the application speed or the volume of dry air.

The adhering interface between the porous insulating film and anelectrode surface is described below in detail.

Desirably, voids capable of retaining a non-aqueous electrolyte areformed on the adhering interface between the porous insulating film andan electrode surface. Due to the retention of a non-aqueous electrolyteby these voids, satisfactory ion conductivity is ensured in an electrodeto which the porous insulating film is adhered, and the battery canmaintain satisfactory discharge characteristic.

In a conventional battery including no porous insulating film, voidscapable of retaining a non-aqueous electrolyte exist between theasperity that is inevitably formed on an electrode surface and theseparator. These voids are presumed to serve to impart satisfactory ionconductivity to the electrode which is adjacent to the separator. Inorder to adhere the porous insulating film to the electrode surfacewhile retaining the voids derived from the asperity of such electrodesurface and to maintain satisfactory ion conductivity in the electrode,the conditions for forming the porous insulating film on the electrodesurface should be appropriately selected.

The conditions for forming the porous insulating film on the electrodesurface can be appropriately adjusted by controlling the viscosity ofthe porous film paint or the conditions for drying the film of theporous film paint (e.g., temperature, volume of air, time). Thoseskilled in the art can control the above conditions such thatpredetermined voids are formed on the adhering interface between theporous insulating film and the electrode surface to which the porousinsulating film is adhered.

From the viewpoint of ensuring the mass productivity of the battery,desirably, the void formed on the adhering interface between the porousinsulating film and the electrode surface to which the porous insulatingfilm is adhered has a size of 1 to 4 μm when measuring the size using amercury intrusion porosimeter. This is because it is relatively easy tocontrol the above conditions so as to form the void having the abovesize and because a void having a size of 1 to 4 μm sufficiently exhibitsthe function to retain a non-aqueous electrolyte.

In other words, the void size distribution of the adhering interfacemeasured by a mercury intrusion porosimeter desirably has a peak in aregion ranging from 1 to 4 μm. When the void size distribution has apeak at less than 1 μm, the size of the voids will be small, and theirfunction to store a non-aqueous electrolyte tends to be low. Conversely,when the void size distribution has a peak at greater than 4 μm, theadhering area between the porous insulating film and the electrodesurface will be small and the adhesion therebetween will be low.Accordingly, the possibility that the porous insulating film might beseparated from the electrode surface increases.

In order to form a void having a size of 1 to 4 μm on the adheringinterface, desirably, the surface roughness of the electrode surface towhich the porous insulating film is adhered is appropriately adjusted.Specifically, the average value Ra of the surface roughness of theelectrode surface measured by a surface roughness measuring instrumentis desirably 0.1 to 1 μm, more desirably 0.2 to 0.8 μm. When the Ra isless than 0.1 μm, the electrode surface serving as the base for theporous insulating film will be excessively smooth, and it might bedifficult to form a void having a size of 1 μm or greater on theadhering interface. Conversely, when the Ra exceeds 1 μm, the electrodesurface serving as the base will be excessively nonuniform and theadhering area between the electrode surface and the porous insulatingfilm will be excessively small, and it might be difficult to form a voidhaving a size of 4 μm or less on the adhering interface.

The rate of the void volume on the adhering interface to the totalvolume of pores of the porous insulating film is preferably 15 to 25%.As used herein, the void volume on the adhering interface is a valuemeasured by a mercury intrusion porosimeter, and the total volume ofpores of the porous insulating film is also a value measured by amercury intrusion porosimeter.

The porous insulating film preferably has a thickness of 2 to 10 μmregardless of the shape of the filler, more preferably 3 to 7 μm. Whenthe porous insulating film has a thickness of 2 to 10 μm, particularlysatisfactory balance of improved safety by the porous insulating filmand energy density of the battery can be maintained. When the porousinsulating film has a thickness of less than 2 μm, the thermalresistance of the porous insulating film will be low. Conversely, whenthe porous insulating film has a thickness of exceeding 10 μm, thevolume of an electrode group composed of electrode plates, the porousinsulating film and a separator will increase, and the energy density ofthe battery will be low.

The negative electrode is formed by placing, on a negative electrodecurrent collector, a material mixture layer containing: a negativeelectrode active material composed of at least a material capable ofabsorbing and desorbing lithium ions; a negative electrode binder; and athickener. Examples of the negative electrode active material include,but not limited to, carbon materials such as any natural graphite, anyartificial graphite, petroleum coke, carbon fiber and a baked organicpolymer, oxides, a silicon or tin-containing composite material such assiliside, a silicon-containing composite material, any metal materialand any alloy material. They may be used singly or in any combination oftwo or more.

Although not specifically limited, the negative electrode binder ispreferably rubber particles because even a small amount thereof issufficient to provide the binding capability. Particularly, thosecontaining a styrene unit and a butadiene unit are preferred. Examplesinclude styrene-butadiene copolymer (SBR) and a modified form of SBRcontaining an acrylic acid unit or acrylate unit. They may be usedsingly or in any combination of two or more.

When rubber particles are used as the negative electrode binder, athickener composed of a water soluble polymer is preferably used withthe rubber particles. The water soluble polymer is preferably acellulose resin, more preferably CMC. The amounts of the rubberparticles and the thickener contained in the negative electrode arepreferably 0.1 to 5 parts by weight per 100 parts by weight of thenegative electrode active material, respectively. As the negativeelectrode binder, other than those mentioned above, PVDF or a modifiedform of PVDF may be used.

As the negative electrode current collector, a metal foil stable under anegative electrode potential such as a copper foil, or a film having ametal (e.g., copper) disposed on the surface thereof can be used. Thesurface of the negative electrode current collector may be roughened toform recesses and projections or the current collector may be punched.

The positive electrode is formed by placing, on a positive electrodecurrent collector, a material mixture layer containing: a positiveelectrode active material composed of at least a lithium compositeoxide; a positive electrode binder; and a conductive material. Examplesof the lithium composite oxide include, but not limited to, lithiumcobalt oxide (LiCoO₂), modified forms of lithium cobalt oxide, lithiumnickel oxide (LiNiO₂), modified forms of lithium nickel oxide, lithiummanganese oxide (LiMn₂O₂), modified forms of lithium manganese oxide,any of the above-listed oxides in which Co, Ni or Mn is partiallyreplaced with other transition metal element, or with a typical metalsuch as aluminum or magnesium; and a compound containing iron as themain constituent element which is referred to as olivinic acid. They maybe used singly or in any combination of two or more.

The positive electrode binder is not specifically limited. Examplesinclude polytetrafluoroethylene (PTFE), modified forms of PTFE, PVDF,modified forms of PVDF, and modified acrylonitrile rubber particles.They may be used singly or in any combination of two or more.Preferably, PTFE is used with a thickener. As the thickener, preferredare CMC, polyethylene oxide (PEO), and modified acrylonitrile rubber(e.g. BM-720H (trade name) available from ZEON CORPORATION).

As the conductive material, acetylene black, ketjen black or anygraphite can be used. They may be used singly or in any combination oftwo or more.

As the positive electrode current collector, a metal foil stable under apositive electrode potential such as an aluminum foil, or a film havinga metal (e.g., aluminum) disposed on the surface thereof can be used.The surface of the positive electrode current collector may be roughenedto form recesses and projections or the current collector may bepunched.

The non-aqueous electrolyte is preferably prepared by dissolving alithium salt in a non-aqueous solvent. The concentration of the lithiumsalt dissolved in the non-aqueous solvent is usually 0.5 to 2 mol/L. Asthe lithium salt, preferably used are lithium hexafluorophosphate(LiPF₆), lithium perchlorate (LiClO₄) and lithium tetrafluoroborate(LiBF₄). They may be used singly or in any combination of two or more.

As the non-aqueous solvent, ethylene carbonate (EC), propylene carbonate(PC), dimethyl carbonate (DMC), diethyl carbonate (DEC) and ethyl methylcarbonate (EMC) are preferred for use. The non-aqueous solvents arepreferably used in a combination of two or more.

In order to form a satisfactory film on an electrode so as to ensurestability during overcharge, it is preferred to add, to the non-aqueouselectrolyte, vinylene carbonate (VC), cyclohexyl benzene (CHB), amodified form of VC or CHB or the like.

The present invention will be described in greater detail below withreference to examples, but it should be understood that the presentinvention is not limited to the examples given below.

Example 1

(i) Production of Positive Electrode

A positive electrode material mixture paste was prepared by mixing withstirring 3 kg of lithium cobalt oxide (positive electrode activematerial), 1 kg of #1320 (trade name) available from Kureha ChemicalIndustry Co., Ltd. (an NMP solution containing 12% by weight PVDF(positive electrode binder)), 90 g of acetylene black (conductivematerial) and an appropriate amount of NMP with the use of a double armkneader. This paste was applied onto both surfaces of a 15 μm thickaluminum foil (positive electrode current collector) except for thepositive electrode lead connecting part. The dried coating layers wererolled by rollers to form positive electrode material mixture layers.Thereby, a positive electrode hoop was obtained. The electrode platecomposed of the aluminum foil and the positive electrode materialmixture layers had a thickness of 160 μm. Thereafter, the positiveelectrode hoop was cut into a size of 60 mm in width and 500 mm inlength. A lead was connected thereto to obtain a positive electrodeplate.

(ii) Production of Negative Electrode

A negative electrode material mixture paste was prepared by mixing withstirring 2 kg of artificial graphite (negative electrode activematerial), 75 g of BM-400B (trade name) available from ZEON CORPORATION(an aqueous dispersion containing 40% by weight modified form ofstyrene-butadiene copolymer (negative electrode binder)), 30 g of CMC(thickener) and an appropriate amount of water with the use of a doublearm kneader. This paste was applied onto both surfaces of a 10 μm thickcopper foil (negative electrode current collector) except for thenegative electrode lead connecting part. The dried coating layers wererolled by rollers to form negative electrode material mixture layers.Thereby, a negative electrode hoop was obtained. The electrode platecomposed of the copper foil and the negative electrode material mixturelayers had a thickness of 180 μm.

(iii) Formation of Porous Insulating Film

A porous film paint was prepared by mixing with stirring 950 g of aninorganic oxide filler, 625 g of BM-720H (trade name) available fromZEON CORPORATION (a solution containing 12% by weight polyacrylonitrilederivative (film binder)) and an appropriate amount of NMP with the useof a double arm kneader. This paste was applied onto both surfaces ofthe negative electrode hoop, which was then dried to form porousinsulating layers each having a thickness of 5 μm. Thereafter, thenegative electrode hoop was cut into a size of 62 mm in width and 570 mmin length. A lead was connected thereto to obtain a negative electrodeplate.

Seven different negative electrode plates having porous insulatinglayers with a porosity P of 0.30, 0.35, 0.40, 0.45, 0.55, 0.60 and 0.65were produced by using, as the inorganic filler, alumina powders havinga bulk density (tap density) of 0.08 g/cm³, 0.2 g/cm³, 0.6 g/cm³, 0.9g/cm³, 1.2 g/cm³, 1.5 g/cm³ and 1.7 g/cm³, respectively.

(iv) Production of Electrode Group

As the separator, six different polypropylene microporous films (filmthickness: 16 μm) were used. These separators had a ratio R of actualvolume to apparent volume of 0.40, 0.45, 0.55, 0.60, 0.65 and 0.70,respectively. The seven negative electrodes and the six separatorsobtained above were combined to form different combinations such thatthe R value of the separator and the P value of the porous insulatingfilm satisfy −0.10≦R−P≦=0.30 as listed in Table 1. Electrode groups wereproduced by spirally winding the positive electrode and each of thecombinations of the negative electrode and the separator.

Each of the obtained electrode groups was inserted in a cylindricalbattery case having a diameter of 18 mm and a height of 67 mm. Leadswere connected to predetermined portions. An electrolyte was theninjected therein in an amount of 5.5 g. The electrolyte was prepared bydissolving LiPF₆ in a solvent mixture comprising ethylene carbonate (EC)and ethyl methyl carbonate (EMC) at a volume ratio of 1:3 at a LiPF₆concentration of 1 mol/L. Thereafter, the opening of the battery casewas sealed with a sealing plate to produce a cylindrical battery havinga design capacity of 2000 mAh and a size of 18 mm in diameter and 65 mmin height.

Comparative Example 1

Five different negative electrode plates having porous insulating layerswith a porosity P of 0.30, 0.35, 0.55, 0.60 and 0.65 were produced inthe same manner as in Example 1 except that, as the inorganic oxidefiller, alumina powders having a bulk density (tap density) of 0.08g/cm³, 0.2 g/cm³, 0.6 g/cm³, 1.5 g/cm³ and 1.7 g/cm³ were used,respectively. As the separator, four different polypropylene microporousfilms (thickness: 16 μm) having a ratio R of actual volume to apparentvolume of 0.40, 0.45, 0.65 and 0.70 were used.

The five negative electrodes and the four separators obtained above werecombined to form different combinations such that the R value of theseparator and the P value of the porous insulating film satisfy 0.35<R−Por R−P<−0.15 as listed in Table 1. Electrode groups with thecombinations were produced in the same manner as in Example 1. Finally,cylindrical batteries were produced.

TABLE 1 R-P P 0.30 0.35 0.40 0.45 0.55 0.60 0.65 R 0.70 0.40* 0.35* 0.300.25 0.15 0.10 0.05 0.65 0.35* 0.30 0.25 0.20 0.10 0.05 0.00 0.60 0.300.25 0.20 0.15 0.05 0.00 −0.05 0.55 0.25 0.20 0.15 0.10 0.00 −0.05 −0.100.45 0.15 0.10 0.05 0.00 −0.10 −0.15* −0.20* 0.40 0.10 0.05 0.00 −0.05−0.15* −0.20* −0.25* The asterisks (*) indicate Comparative Example.[Evaluation 1]

The batteries produced in Example 1 and Comparative Example 1 weresubjected to the following evaluation tests.

(Low Temperature Discharge Test)

Each battery was charged at a constant voltage of 4.2 V with a maximumcurrent of 1400 mA at an environmental temperature of 20° C. for 2hours, and then discharged at a constant current of 2000 mA with anend-of-discharge voltage of 3.0 V at an environmental temperature of 20°C. The discharge capacity at 20° C. was measured. Subsequently, thebattery having been discharged at 20° C. was again charged under thesame conditions as above, after which the charged battery was cooleddown at an environmental temperature of −10° C. for 6 hours. The batteryhaving cooled down was discharged at a constant current of 2000 mA withan end-of-discharge voltage of 3.0 V at an environmental temperature of−10° C. Then, the discharge capacity at −10° C. was measured. The rateof the discharge capacity at −10° C. to the discharge capacity at 20° C.was calculated in percentage (%), which was referred to as lowtemperature discharge retention rate (−10° C./−20° C. discharge capacityratio). The results are shown in Table 2.

(Shut-Down Test)

Each battery was charged at a constant voltage of 4.2 V with a maximumcurrent of 1400 mA at an environmental temperature of 20° C. for 2hours. Subsequently, the AC impedance of the battery in an open circuitcondition was monitored while the temperature in the thermostaticchamber was increased. The internal resistance of the battery wasmeasured when the battery shut down. The results are shown in Table 3.

TABLE 2 −10° C./20° C. discharge capacity ratio (%) P 0.30 0.35 0.400.45 0.55 0.60 0.65 R 0.70 45 55 65 75 83 85 89 0.65 53 69 75 80 88 9094 0.60 61 78 84 87 91 94 94 0.55 70 79 85 88 92 94 95 0.45 76 82 88 9194 95 96 0.40 78 83 89 92 95 95 96

TABLE 3 Internal resistance at the time of shut-down (Ω) P 0.30 0.350.40 0.45 0.55 0.60 0.65 R 0.70 10⁻⁵ 10⁻⁵ 10⁻⁵ 10⁻⁵ 10⁻⁵ 10⁻⁵ 10⁻⁵ 0.6510⁻⁵ 10⁻⁵ 10⁻⁵ 10⁻⁵ 10⁻⁵ 10⁻⁵ 10⁻⁵ 0.60 10⁻⁵ 10⁻⁵ 10⁻⁵ 10⁻⁵ 10⁻⁵ 10⁻⁵10⁻⁵ 0.55 10⁻⁵ 10⁻⁵ 10⁻⁵ 10⁻⁵ 10⁻⁵ 10⁻⁵ 10⁻⁵ 0.45 10⁻⁵ 10⁻⁵ 10⁻⁵ 10⁻⁵10⁻⁵ 10⁻³ 10⁻³ 0.40 10⁻⁵ 10⁻⁵ 10⁻⁵ 10⁻⁵ 10⁻³ 10⁻³ 10⁻²

As seen from Table 2, the batteries having an R−P value of 0.35 or moreexhibited a significantly decreased low temperature discharge retentionrate of not greater than 60%. This indicates that, in order to obtainbatteries having excellent low temperature discharge characteristic, thebatteries should be designed to satisfy R−P≦0.30. Likewise, as seen fromTable 3, the batteries having an R−P value of or less exhibited a lowinternal resistance of 10⁻³Ω or less when the batteries shut down. Incontrast, the batteries having an R−P value of −0.10 or greater achieveda high internal resistance of 10⁻⁵Ω or higher, and satisfactoryshut-down effect was obtained. The foregoing indicates that batterieshaving excellent low temperature discharge characteristic andsatisfactory shut-down characteristic can be obtained by satisfying0.4≦R≦0.7 and −0.10≦R−P≦0.30.

Example 2

(i) Production of Positive Electrode

A positive electrode material mixture paste was prepared by mixing withstirring 3 kg of lithium cobalt oxide (positive electrode activematerial), 1 kg of #1320 (trade name) available from Kureha ChemicalIndustry Co., Ltd. (an NMP solution containing 12% by weight PVDF(positive electrode binder)), 90 g of acetylene black (conductivematerial) and an appropriate amount of NMP with the use of a double armkneader. This paste was applied onto both surfaces of a 15 μm thickaluminum foil (positive electrode current collector) except for thepositive electrode lead connecting part. The dried coating layers wererolled by rollers to form positive electrode material mixture layers.During the formation of the positive electrode material mixture layers,the thickness of the electrode plate composed of the aluminum foil andthe positive electrode material mixture layers was controlled to be 160μm. Then, the electrode plate was cut so as to have a width which wouldallow insertion thereof into a battery can for cylindrical battery(18650 type). Thereby, a positive electrode hoop was obtained.

(ii) Production of Negative Electrode

A negative electrode material mixture paste was prepared by mixing withstirring 2 kg of artificial graphite (negative electrode activematerial), 75 g of BM-400B (trade name) available from ZEON CORPORATION(an aqueous dispersion containing 40% by weight modified form ofstyrene-butadiene copolymer (negative electrode binder)), 30 g of CMC(thickener) and an appropriate amount of water with the use of a doublearm kneader. This paste was applied onto both surfaces of a 10 μm thickcopper foil (negative electrode current collector) except for thenegative electrode lead connecting part. The dried coating layers wererolled by rollers to form negative electrode material mixture layers.During the formation of the negative electrode material mixture layers,the thickness of the electrode plate composed of the copper foil and thenegative electrode material mixture layers was controlled to be 180 μm.Then, the electrode plate was cut so as to have a width which wouldallow insertion thereof into a battery can for cylindrical battery(18650 type). Thereby, a negative electrode hoop was obtained.

(iii) Formation of Porous Insulating Film

Alumina AA03 (trade name) available from Sumitomo Chemical Co., Ltd.(primary particles of α-alumina with a volume based median size: D50 of0.3 μm) was heated at 900° C. for 1 hour so as to allow the primaryparticles to diffuse and bond together. Thereby, polycrystallineparticles were obtained. The obtained polycrystalline particles had avolume based median size: D50 of 2.6 μm.

Three hundred grams of the obtained polycrystalline particles (inorganicoxide filler) and 12 g of solid content of BM720H (trade name) availablefrom ZEON CORPORATION (a solution containing 12% by weightpolyacrylonitrile derivative (film binder)) were mixed (i.e., 4 parts byweight film binder per 100 parts by weight polycrystalline particles)with stirring with an appropriate amount of NMP with the use of a doublearm kneader having an internal volume of 300 ml (T.K.HIVIS MIX f model.1available from Tokushu Kika Kogyo Co, Ltd), whereby first mixing wasperformed for 30 minutes with a solid content of 60% by weight.Thereafter, NMP was further added to the primary mixture, and secondmixing was performed at a solid content of 30% by weight. Thereby, aporous film paint was prepared.

This paint was applied onto both surfaces of the negative electrode hoopby gravure roll method at a rate of 0.5 m/min., which was then dried byhot air blown at a rate of 0.5 m/sec., whereby a porous insulating filmhaving a thickness of 10 μm was formed on each surface of the negativeelectrode. The porous insulating film had a porosity P of 0.6.

(iv) Preparation of Non-aqueous Electrolyte

A non-aqueous electrolyte was prepared by dissolving LiPF₆ in anon-aqueous solvent mixture comprising ethylene carbonate (EC), dimethylcarbonate (DMC) and ethyl methyl carbonate (EMC) at a volume ratio of2:3:3 at a LiPF₆ concentration of 1 mol/L. Further, VC was added theretoin an amount of 3 parts by weight per 100 parts by weight of thenon-aqueous electrolyte.

(v) Production of Battery

Using the positive electrode, negative electrode and non-aqueouselectrolyte produced above, a 18650 type cylindrical battery wasproduced in the following procedure. The positive and negativeelectrodes were first cut into a predetermined length. One end of apositive electrode lead was connected to the positive electrode leadconnecting part. One end of a negative electrode lead was connected tothe negative electrode lead connecting part. Subsequently, the positiveand negative electrodes were spirally wound with a separator made of apolyethylene resin microporous film having a thickness of 16 μminterposed therebetween to form a columnar electrode group. The outersurface of the electrode group was wrapped by the separator. Thiselectrode group, which was sandwiched by an upper insulating ring and alower insulating ring, was housed in a battery can.

The ratio R of actual volume to apparent volume of the separator was0.6. Accordingly, the R−P value was 0.

Subsequently, the non-aqueous electrolyte described above was weighed5.5 g, which was then injected into the battery can in two separateinjection steps. In each injection step, the pressure was reduced to 133Pa so as to impregnate the electrode group with the non-aqueouselectrolyte. In the first injection step, 5 g of the non-aqueouselectrolyte was injected into the battery can, and in the secondinjection step, 0.5 g was injected.

The other end of the positive electrode lead was welded to the undersideof a battery lid. The other end of the negative electrode lead waswelded to the inner bottom surface of the battery can. Finally, theopening of the battery can was sealed with the battery lid equipped withan insulating packing therearound. Thereby, a cylindrical lithium ionsecondary battery having a theoretical capacity of 2 Ah was produced.

Comparative Example 2

A battery was produced in the same manner as in Example 2 except that noporous insulating film was formed on the negative electrode surface.

Comparative Example 3

A battery was produced in the same manner as in Example 2 except that,as the inorganic oxide filler of the porous insulating film, primaryparticles of Alumina AA03 (trade name) available from Sumitomo ChemicalCo., Ltd. were used intact without any heating. The porous insulatingfilm had a porosity P of 0.35. Accordingly, the R−P value was 0.25.

Example 3

Batteries were produced in the same manner as in Example 2 except that,in the preparation of the porous film paint, the time for the firstmixing was changed to 10, 20, 45 and 60 minutes. The porous insulatingfilms had a porosity P of 0.60, 0.60, 0.58 and 0.55, respectively.Accordingly, the R−P values were 0, 0, 0.02 and 0.05.

Example 4

Batteries were produced in the same manner as in Example 2 except thatthe amount of BM720H serving as the film binder contained in the porousinsulating film was changed to 0.5, 1, 2, and 6 parts by weight on asolid content basis per 100 parts by weight of the polycrystallinealumina particles. The porous insulating films had a porosity P of 0.62,0.61, 0.60 and 0.56, respectively. Accordingly, the R−P values were−0.02, −0.01, 0 and 0.04.

Example 5

A battery was produced in the same manner as in Example 2 except that,as the inorganic oxide filler of the porous insulating film, TA300(trade name) (polycrystalline titania particles with a volume basedmedian size: D50 of 0.4 μm where the primary particles had an averageparticle size of 0.1 μm) available from Fuji Titanium Industry Co., Ltd.was used. The porous insulating film had a porosity P of 0.48.Accordingly, the R−P value was 0.12.

[Evaluation 2]

The batteries produced in Examples 2 to 5 and Comparative Examples 2 and3 were subjected to the following evaluation tests.

(Outward Appearance of Porous Insulating Film)

After the application of the porous film paint onto the negativeelectrode and drying were performed, the porous insulating film wasvisually checked for the condition immediately after the formation. Theporous insulating film exhibiting a problem such as separation was ratedas “changed”. The rest was rated as “no change”. Table 4 shows therelation among the time for the first mixing in the preparation step ofthe porous film paint, the amount of the film binder expressed in partsby weight per 100 parts by weight of the inorganic oxide filler, and theoutward appearance of the negative electrode.

(Pore Size D90)

Using a mercury intrusion porosimeter (9410) available from SHIMADZUCORPORATION, the pore size distribution of the negative electrode havingthe porous insulating film adhered thereon was measured. As a result,the sum of the pore size distribution of the porous insulating film andthat of the negative electrode was obtained. Meanwhile, the pore sizedistribution of the negative electrode before the porous insulating filmwas formed was measured. Subsequently, the pore size distribution of theporous insulating film alone was calculated by subtracting the pore sizedistribution of the negative electrode alone from the sum of the poresize distribution of the porous insulating film and that of the negativeelectrode. From the above-obtained pore size distribution of the porousinsulating film alone, 90% cumulative volume pore size D90 wasdetermined.

(Discharge Characteristic)

The finally produced batteries including electrode groups without anyfracture, crack or separation due to the spiral winding process weresubjected to pre-charge/discharge twice, after which they were stored inan environment of 45° C. for 7 days. Thereafter, the batteries weresubjected to the following two different patterns of charge/discharge inan environment of 20° C.

(1) First Pattern

Constant current charge: 1400 mA (end voltage: 4.2 V)

Constant voltage charge: 4.2 V (end current: 100 mA)

Constant current discharge: 400 mA (end voltage: 3 V)

(2) Second Pattern

Constant current charge: 1400 mA (end voltage: 4.2 V)

Constant voltage charge: 4.2 V (end current: 100 mA)

Constant current discharge: 4000 mA (end voltage: 3 V)

The rate (capacity ratio) of the discharge capacity at 4000 mA to thedischarge capacity at 400 mA was calculated in percentage as a measurefor discharge characteristic. The larger capacity ratio the battery has,the better the discharge characteristic. Table 5 shows the relationbetween 90% cumulative volume pore size D90 in the pore sizedistribution of the porous insulating film contained in each battery andthe discharge characteristic of each battery.

(Nail Penetration Test)

The batteries having undergone the charge/discharge characteristicevaluation were charged as follows.

Constant current charge: 1400 mA (end voltage: 4.25 V)

Constant voltage charge: 4.25 V (end current: 100 mA)

Each of the charged batteries was pierced by a round iron nail with adiameter of 2.7 mm from the side thereof in an environment of 20° C. ata speed of 5 mm/sec. or 180 mm/sec., after which the heat generation wasobserved. The temperature of the pierced portion of the battery wasmeasured 1 second and 90 seconds after the piercing of the battery.Table 6 shows the results of the nail penetration test for each battery.

TABLE 4 Outward appearance Time for Film binder of porous Inorganicoxide first mixing parts by insulating filler (min) weight film Ex. 2Polycrystalline 30 4 No change alumina particles Ex. 3 Polycrystalline10 4 Changed alumina particles Polycrystalline 20 4 No change aluminaparticles Polycrystalline 45 4 No change alumina particlesPolycrystalline 60 4 No change alumina particles Ex. 4 Polycrystalline30 0.5 Changed alumina particles Polycrystalline 30 1 No change aluminaparticles Polycrystalline 30 2 No change alumina particlesPolycrystalline 30 6 No change alumina particles Ex. 5 Polycrystalline30 4 No change titania particles Comp. — — — — Ex. 2 Comp. Aluminaprimary 30 4 No change Ex. 3 particles

TABLE 5 −10° C./20° C. discharge Pore size D90 (μm) capacity ratio (%)Ex. 2 0.23 94 Ex. 3 0.34 94 0.28 93 0.17 92 0.14 88 Ex. 4 0.32 95 0.2994 0.26 94 0.13 87 Ex. 5 0.22 93 Comp. — 95 Ex. 2 Comp. 0.10 85 Ex. 3

TABLE 6 Nail penetration test Nail piercing speed Nail piercing speed 5mm/sec. 180 mm/sec. Temperature Temperature Temperature Temperature 1second after 90 second 1 second after 90 second (° C.) after (° C.) (°C.) after (° C.) Ex. 2 75 87 74 88 Ex. 3 76 88 74 84 78 89 75 83 74 8770 85 79 88 74 87 Ex. 4 80 88 75 84 77 89 68 85 76 91 75 85 78 91 76 85Ex. 5 78 90 74 86 Comp. 149 — 137 — Ex. 2 Comp. 77 94 75 87 Ex. 3

The evaluation results are discussed below.

The battery having the negative electrode of Comparative Example 2without the porous insulating film exhibited a significant temperaturerise when the battery was pierced by the nail especially at a low rate.This is because the conventional polyethylene resin separator melted dueto heat generated during short circuit caused by the penetration of thenail, and the short-circuited area was enlarged.

The negative electrode of Comparative Example 3 having the porousinsulating film formed on the negative electrode surface exhibitedsatisfactory result in the nail penetration test. It was, however,significantly inferior to that of Comparative Example 2 in terms ofdischarge characteristic. This is because the porous insulating film ofComparative Example 2 had too small a pore size D 90 measured by themercury intrusion porosimeter, namely 0.10 μm. Presumably, when the poresize D90 is excessively small, the porous insulating film cannotmaintain its capability to retain electrolyte or ion conductivitysufficiently after the swelling of the film binder.

Contrary to Comparative Examples 2 and 3, the battery of Example 2having the porous insulating film made of inorganic oxide fillercomposed of polycrystalline alumina particles and a small amount of filmbinder achieved results almost equal to those of Comparative Example 2in terms of safety in the event of nail penetration and dischargecharacteristic. This is because the porous insulating film of Example 2had a sufficiently large pore size D90 of 0.23 μm, so that thecapability to retain electrolyte or ion conductivity of the porousinsulating film was ensured sufficiently even after the swelling of thefilm binder. The battery of Example 5 having the inorganic oxide fillercomposed of, instead of alumina, polycrystalline titania particlesexhibited similar results as that of Example 2.

The results of Example 3 indicate that, when the time for the firstmixing was excessively long in the preparation step of the porous filmpaint, the film binder was excessively dispersed and the pore size D90became small, failing to achieve a high level of dischargecharacteristic. Conversely, when the time for the first mixing wasexcessively short, satisfactory discharge characteristic and safety inthe event of nail penetration were obtained, but the separation of theporous insulating film was observed. Presumably, this is because thefirst mixing was insufficient and the film binder coagulatedexcessively: as a result, the adhesion strength was low.

The results of Example 4 indicate that, when the amount of the filmbinder was excessively large, the pore size D90 became small, failing toachieve a high level of discharge characteristic. Conversely, when theamount of the film binder was reduced to 0.5 parts by weight per 100parts by weight of the inorganic oxide filler, although satisfactorydischarge characteristic and safety in the event of nail penetrationwere obtained, the separation of the porous insulating film wasobserved. This is presumably because the adhesion strength wasinsufficient.

Although the electrode plate portion without the separation of theporous insulating film is usable for the production of batteries, fromthe viewpoint of preventing the reduction of the production yield, it isdesirable to perform the first mixing properly and to use the filmbinder in an amount of at least 1 part by weight or more per 100 partsby weight of the inorganic oxide filler.

Example 6

(i) Production of Positive Electrode

A positive electrode material mixture paste was prepared by mixing withstirring 3 kg of lithium cobalt oxide (positive electrode activematerial), 1 kg of #1320 (trade name) available from Kureha ChemicalIndustry Co., Ltd. (an NMP solution containing 12% by weight PVDF(positive electrode binder)), 90 g of acetylene black (conductivematerial) and an appropriate amount of NMP with the use of a double armkneader. This paste was applied onto both surfaces of a 15 μm thickaluminum foil (positive electrode current collector) except for thepositive electrode lead connecting part. The dried films were rolled byrollers to form positive electrode material mixture layers. Thereby, apositive electrode hoop was produced. During the formation of thepositive electrode material mixture layers, the thickness of theelectrode plate composed of the aluminum foil and the positive electrodematerial mixture layers was controlled to be 160 μm. Then, the electrodeplate was cut into a size of 60 mm in width and 500 mm in length toobtain a positive electrode.

(ii) Production of Negative Electrode

A negative electrode material mixture paste was prepared by mixing withstirring 2 kg of artificial graphite (negative electrode activematerial), 75 g of BM-400B (trade name) available from ZEON CORPORATION(an aqueous dispersion containing 40% by weight modified form ofstyrene-butadiene copolymer (negative electrode binder)), 30 g of CMC(thickener) and an appropriate amount of water with the use of a doublearm kneader. This paste was applied, by die coating method, onto bothsurfaces of a 10 μl thick copper foil (negative electrode currentcollector) except for the negative electrode lead connecting part. Here,the paste was applied onto the copper foil at a speed of 0.2 m/min. Thecopper foil having coating layers formed thereon was passed through adrying oven at the same speed as above to dry the coating layers. Thedried coating layers were rolled by rollers to form negative electrodematerial mixture layers. Thereby, a negative electrode hoop wasproduced. During the formation of the negative electrode materialmixture layers, the thickness of the electrode plate composed of thecopper foil and the negative electrode material mixture layers wascontrolled to be 180 μm. The obtained negative electrode materialmixture layers had an average surface roughness Ra of 0.21 μm. Theaverage surface roughness Ra was measured using “Surfcom”, a surfaceroughness measuring instrument available from TOKYO SEIMITSU CO., LTD.

(iii) Formation of Porous Insulating Film

As the inorganic oxide filler, alumina having an average particle size(volume based median size: D50) of 0.5 μm and a bulk density (tapdensity) of 0.6 g/cm³ was used. A porous film paint was prepared bymixing with stirring 950 g of the inorganic oxide filler, 475 g ofBM720H (trade name) available from ZEON CORPORATION (an NMP solutioncontaining 8% by weight polyacrylonitrile derivative (film binder))(i.e., 4 parts by weight film binder per 100 parts by weightpolycrystalline particles) and 2725 g of NMP with the use of a doublearm kneader.

The obtained porous film paint was applied onto both surfaces of theabove-produced negative electrode hoop by gravure roll method at a speedof 1 m/min., which was then dried by hot air at 150° C. blown at an airflow rate of 10 m/sec., whereby a porous insulating film having athickness of 5 μm and adhered on each surface of the negative electrodewas formed. Thereafter, the negative electrode hoop having the porousinsulating films adhered to both surfaces thereof was cut into a size of62 mm in width and 570 mm in length to produce a negative electrodehaving the porous insulating films adhered to both surfaces thereof. Theporous insulating films had a porosity P of 0.55.

(iv) Preparation of Non-aqueous Electrolyte

A non-aqueous electrolyte was prepared by dissolving LiPF₆ in anon-aqueous solvent mixture comprising ethylene carbonate (EC) and ethylmethyl carbonate (EMC) at a volume ratio of 1:3 at a LiPF₆ concentrationof 1 mol/L. Further, VC was added thereto in an amount of 3 parts byweight per 100 parts by weight of the non-aqueous electrolyte.

(v) Production of Battery

Using the positive electrode, negative electrode and non-aqueouselectrolyte produced above, a cylindrical lithium ion secondary batterywas produced in the following procedure. Firstly, one end of a positiveelectrode lead was connected to the positive electrode lead connectingpart. One end of a negative electrode lead was connected to the negativeelectrode lead connecting part. Subsequently, the positive and negativeelectrodes were spirally wound with a separator made of a polypropyleneresin microporous film (thickness: 16 μm, porosity: 45% (R=0.55))interposed therebetween to form a columnar electrode group. The outersurface of the electrode group was wrapped by the separator. Thiselectrode group, which was sandwiched by an upper insulating ring and alower insulating ring, was housed in a cylindrical battery can having adiameter of 18 mm and a height of 670 mm.

The ratio R of actual volume to apparent volume of the separator was0.55. Accordingly, the R−P value was 0.

The other end of the positive electrode lead was welded to the undersideof a battery lid equipped with an insulating packing therearound. Theother end of the negative electrode lead was welded to the inner bottomsurface of the battery can. Finally, the opening of the battery can wassealed with the battery lid. Subsequently, the above-preparednon-aqueous electrolyte was injected from an injection inlet of thebattery lid into the battery can in two separate injection steps. Ineach injection step, the pressure was reduced to 133 Pa so as toimpregnate the electrode group with the non-aqueous electrolyte. In thefirst injection step, 5 g of the non-aqueous electrolyte was injectedinto the battery can, and in the second injection step, 0.5 g wasinjected. Finally, the injection inlet was sealed. Thereby, acylindrical lithium ion secondary battery (hereinafter referred to asbattery 1) was produced.

Comparative Example 4

A battery (hereinafter referred to as battery R) was produced in thesame manner as in Example 6 except that, in the formation step of theporous insulating film, the porous film paint applied onto both surfacesof the negative electrode hoop was dried at a temperature of 40° C. Theporous insulating films had a porosity P of 0.55. Accordingly, the R−Pvalue was 0.

Example 7

Batteries 2, 3, 4, 5 and 6 were produced in the same manner as inExample 6 except that, in the production step of the negative electrode,the speed at which the negative electrode material mixture paste wasapplied onto both surfaces of the copper foil and then dried was changedto 0.05 m/min., 0.1 m/min., 0.5 m/min., 0.8 m/min. and 1.1 m/min., andthat the average surface roughness Ra of the negative electrode materialmixture layers was changed to 0.06 μm, 0.13 μm, 0.62 μm, 0.97 μm and1.24 μm, respectively. The porous insulating films had a porosity P of0.55, 0.55, 0.55, 0.55 and 0.55, respectively. Accordingly, the R−Pvalues were all 0.

[Evaluation 3]

The batteries produced in Examples 6 and 7 and Comparative Example 4were subjected to the following evaluation tests.

(Separation of Porous Insulating Film)

The outward appearance of the porous insulating film formed on thenegative electrode surface immediately after the drying was visuallychecked to see if there was any separation.

(SEM Observation)

The negative electrode having the porous insulating films adheredthereon was cut. Without performing any treatment such as metal vapordeposition, the cross section of the negative electrode was observedusing a scanning electron microscope (S-4500 available from Hitachi,Ltd.) at an accelerating voltage of 5 kV.

(Pore Size Distribution)

The negative electrode having the porous insulating films adheredthereon was cut into nine rectangles, each having a size of 2 cm×1 cm.The obtained nine rectangular pieces of the electrode plate were treatedas a single sample, which was introduced into a measurement cell of aporosimeter. The pore size distribution of the sample electrode platewas measured by mercury intrusion method. As the measurement device(porosimeter), Autopore III9410 available from SHIMADZU CORPORATION wasused. The pressure for measurement ranged from 4 to 60000 psia. Underthis pressure condition, the pore size distribution ranging from 0.003to 50 μm can be measured. In the same manner as above, the pore sizedistribution of the negative electrode before the porous insulating filmwas adhered thereon was determined.

(Discharge Characteristic)

Each battery was subjected to discharge test at a low temperature asfollows.

Each battery was charged at a constant voltage of 4.2 V with a maximumcharge current of 1400 mA at an environmental temperature of 20° C. for2 hours, and then discharged at a constant current of 2000 mA with anend-of-discharge voltage of 3.0 V at an environmental temperature of 20°C. Thereby, the discharge capacity at 20° C. was measured.

Subsequently, the battery having been discharged at 20° C. was againcharged under the same conditions as above, after which the chargedbattery was cooled down at an environmental temperature of −10° C. for 6hours. At the same environmental temperature of −10° C., the batteryhaving cooled down was discharged at a constant current of 2000 mA withan end-of-discharge voltage of 3.0 V. Thereby, the discharge capacity at−10° C. was measured.

The rate of the discharge capacity at −10° C. to the discharge capacityat 20° C. was calculated in percentage, and the rate was referred to aslow temperature discharge retention rate (−10° C./20° C. dischargecapacity ratio).

The evaluation results of Examples 6 to 7 and Comparative Example 4 arediscussed below.

FIG. 3 is an SEM image of a cross section of the negative electrode ofComparative Example 4 having the porous insulating films adheredthereon. The upper layer is the porous insulating film. The bottom layeris the negative electrode material mixture layer. A void can hardly befound at the adhering interface between the porous insulating film andthe negative electrode material mixture layer. This is presumablybecause since the application step of the porous insulating film to thenegative electrode surface and the drying step were performed at 40° C.,the paint retained high fluidity for a relatively long time, and theporous film paint infiltrated into the recesses on the negativeelectrode surface: as a result, the recesses were filled with the paint.

FIG. 4 is an SEM image of a cross section of the negative electrode ofExample 6 having the porous insulating films adhered thereon. The upperlayer is the porous insulating film. The bottom layer is the negativeelectrode material mixture layer. At the adhering interface between theporous insulating film and the negative electrode material mixturelayer, relatively large voids are formed. This is presumably because theapplication step of the porous insulating film to the negative electrodesurface and the drying step were performed at 150° C., and the paint hadlost its fluidity so that the paint did not infiltrate into the recesseson the negative electrode surface.

FIG. 5 is a graph showing the pore size distribution (A) for thenegative electrode before the porous insulating films were adhered, thepore size distribution (B) for the sample electrode plate of Example 6having the porous insulating films adhered thereon and the pore sizedistribution (C) for the sample electrode plate of Comparative Example 4having the porous insulating films adhered thereon, all of which weredetermined by the mercury intrusion porosimeter. The distributions (B)and (C) in FIG. 5 include the voids of the porous insulating film, thevoids of the negative electrode and the voids at the adhering interfacebetween the porous insulating film and the electrode surface.

As seen from FIG. 5, in the pore size distribution (A) of the negativeelectrode serving as the base for the porous insulating film, thereexist pores having a diameter of about 2 μm which can be considered asthe asperity on the negative electrode surface. In the pore sizedistribution (C) of the porous insulating film formed through theapplication and drying steps of the porous film paint performed at 40°C., no peak can be found in the range of 1 μm and greater. This suggeststhat the asperity existed on the negative electrode surface was filledwith the porous insulating film. On the other hand, in the pore sizedistribution (B) of the porous insulating film formed through theapplication and drying steps of the porous film paint performed at 150°C., a peak can be seen at about 1.5 μm. This suggests that voids havinga size of about 1.5 μm exist at the adhering interface between theporous insulating film and the negative electrode surface of Example 6.These results agree with those obtained by the SEM observation.

Table 7 shows the information about the negative electrodes and theporous insulating films produced in Examples 6 and 7 and ComparativeExample 4, and the results of the low temperature discharge retentionrate of those batteries. It should be noted that, among the peaks in thepore size distribution, a size that corresponds to a peak that can beattributed to the void at the adhering interface between the porousinsulating film and the negative electrode surface is taken as void sizeat the adhering interface.

TABLE 7 Low temperature discharge Negative electrode Porous insulatingfilm retention rate Application/Drying Application/Drying Size of void−10° C./20° C. speed Ra temperature at adhering Presence of dischargecapacity Battery (m/min.) (μm) (° C.) interface (μm) separation ratio(%) Ex. 6 Battery 1 0.2 0.21 40 None No 88 Comp. Battery R 0.2 0.21 1501.48 No 96 Ex. 4 Ex. 7 Battery 2 0.05 0.06 150 0.72 No 93 Battery 3 0.10.13 150 1.05 No 95 Battery 4 0.5 0.62 150 2.49 No 96 Battery 5 0.8 0.97150 3.87 No 97 Battery 6 1.1 1.24 150 4.92 Partially 97

In the case of Comparative Example 4, the discharge capacity retentionrate at −10° C. was 88% whereas, in Example 6, the discharge capacityretention rate at −10° C. increased to as high as 96%. This is becausethe porous film paint was formed without filling the recesses on thenegative electrode surface, and voids capable of retaining non-aqueouselectrolyte were formed at the adhering interface between the porousinsulating film and the negative electrode surface: as a result,satisfactory ion conductivity was ensured in the negative electrode.

In Example 7, when the average roughness Ra of the negative electrodesurface serving as the base for the porous insulating film was rangedfrom 0.13 to 0.97 μm, the peaks to be attributed to the void formed onthe adhering interface between the porous insulating film and thenegative electrode surface were observed in the range from 1.05 to 3.87μm in the pore size distributions. In this case, low temperaturedischarge retention rates similar to that of Example 6 were achieved.

On the other hand, in Example 7, when the average surface roughness Raof the negative electrode surface was less than 0.1 μm (0.06 μm), thepeak in the pore size distribution to be attributed to the void formedon the adhering interface was observed at 0.72 μm which was relativelysmall. In this case, the low temperature discharge retention ratedecreased to a certain extent compared to that of Example 6.

Further, in Example 7, when the average surface roughness Ra of thenegative electrode surface exceeded 1 μm (1.24 μm), the peak in the poresize distribution to be attributed to the void formed on the adheringinterface was observed at 4.92 μm which was relatively large. In thiscase, satisfactory low temperature discharge retention rate wasobtained, but the separation of the porous insulating film from thenegative electrode surface was found.

From the above, the following is clear. In order to significantlyimprove low temperature discharge retention rate while maintaining theadhesion strength between the porous insulating film and the electrodesurface, it is effective to set the peak to be attributed to the voidformed on the adhering interface between the porous insulating film andthe electrode surface to 1 to 4 μm in the pore size distribution. Tothat end, it is effective to set the average roughness Ra of theelectrode surface to 0.1 to 1 μm.

Industrial Applicability

The non-aqueous electrolyte secondary battery of the present inventionis useful as portable power sources having excellent safety. The presentinvention is suitable for lithium ion secondary batteries including theporous insulating film adhered on the surface of an electrode which arespecifically designed to secure thermal resistance and safety againstshort circuit and the batteries can achieve excellent dischargecharacteristic.

1. A non-aqueous electrolyte secondary battery comprising: a positiveelectrode; a negative electrode; a separator interposed between saidpositive electrode and said negative electrode; a non-aqueouselectrolyte; and a porous insulating film adhering to a surface of atleast one selected from the group consisting of said positive electrodeand said negative electrode, said porous insulating film comprising aninorganic oxide filler and a film binder, wherein a void capable ofretaining said non-aqueous electrolyte is formed on an adheringinterface where said porous insulating film adheres to said electrodesurface, said void having a size of 1 to 4 μm, the amount of said filmbinder contained in said porous insulating film is not greater than 4parts by weight per 100 parts by weight of said inorganic oxide filler,a void size distribution of said negative electrode and said porousinsulating film measured by a mercury intrusion porosimeter has a peakin a region ranging from 1 to 4 μm and said electrode surface to whichsaid porous insulating film adheres has an average surface roughness Raof 0.1 to 1 μm.
 2. The non-aqueous electrolyte secondary battery inaccordance with claim 1, wherein the amount of said film bindercontained in said porous insulating film is not less than 1 part byweight per 100 parts by weight of said inorganic oxide filler.
 3. Thenon-aqueous electrolyte secondary battery in accordance with claim 1,wherein said electrode surface to which said porous insulating filmadheres has an average surface roughness Ra of 0.2 to 0.8 μm.
 4. Thenon-aqueous electrolyte secondary battery in accordance with claim 1,wherein said electrode surface to which said porous insulating filmadheres is a surface of said negative electrode, said negative electrodecomprises a negative current collector and a negative electrode materialmixture layer adhering to said negative electrode current collector,said negative electrode material mixture layer comprises a negativeelectrode active material and a negative electrode binder, and saidnegative electrode active material is at least one selected from thegroup consisting of carbon materials, silicon-containing compositematerials and tin-containing composite materials.